Method of manufacturing martensitic stainless steel

ABSTRACT

The occurrence of delayed fracture which is found in a hot worked martensitic stainless steel is prevented by subjecting the steel, after hot working and prior to heat treatment for hardening by quenching from a temperature of at least Ac 1  point of the steel, to preliminary softening heat treatment under such conditions that the softening parameter P defined below is at least 15,400 and the softening temperature T is lower than the Ac 1  point: 
         P (softening parameter): P=T (20+log  t )         T: softening temperature [K]   t: duration of softening treatment [Hr].
 
The present invention is particularly effective for a martensitic stainless steel having a steel composition in which the amount of effective dissolved C and N (=[C*+10N*]) where C* and N* are calculated by the following formulas is larger than 0.45:
       
       C*=C−[12{(Cr/52)×(6/23)}/10, and
 
       N*=N−[14{(V/51)+(Nb/93)}/10]−[14{(Ti/48)+(B/11)+(Al/27)}/10].

TECHNICAL FIELD

This invention relates to a method of preventing delayed fracture inmartensitic stainless steel which undergoes martensitic transformationeven while it is allowed to cool in air and a method of manufacturing amartensitic stainless steel having such a property of preventing delayedfracture.

BACKGROUND ART

Steel pipes of martensitic stainless steel like API 13Cr-steel hasexcellent corrosion in a CO₂-containing atmosphere, and hence they aremainly used in oil well applications such as tubing and casing for usein excavation of oil wells. Martensitic stainless steel is hardened byquenching from a temperature in the austenite region (at a temperatureequal to or above the Ac₁ point of the steel) to form a martensiticstructure. Therefore, it is normally subjected to final heat treatmentfor hardening after hot working.

However, the high hardenability of a martensitic stainless steel maycause martensitic transformation of the steel even while it is allowedto cool in air after hot working such as pipe formation, and in somecases cracks develop particularly in those portions to which an impacthas been applied during handling of the product. This phenomenon whichis referred to as delayed fracture suddenly takes place after a certainperiod of time has passed from hot working. Therefore, for hot workingof martensitic stainless steel, it is necessary to prevent theoccurrence of delayed fracture during the period after hot working andprior to heat treatment for hardening.

In the manufacture of martensitic stainless steel pipes, a commoncountermeasure against delayed fracture is to limit the length of timefrom the completion of pipe formation up to the start of heat treatmentfor hardening by quenching. To do so, shortly after pipe formation, theresulting pipe must be subjected to heat treatment to provide the steelwith sufficient strength by quenching. However, limiting the time frompipe formation until heat treatment sometimes makes it necessary tofrequently change the heat treatment temperature during operation,leading to a decrease in manufacturing efficiency.

JP 2004-43935A described a martensitic stainless seamless pipe withsuppressed delayed fracture by a technique based on restriction of theamount of effective dissolved C and N (which is defined below) to 0.45or less. However, the amount of effective dissolved C and N isdetermined by the composition of a steel, and when an appropriate steelcomposition is selected by considering other properties such as strengthand toughness, there are cases that the amount of effective dissolved Cand N exceeds 0.45. Therefore, this technique cannot be said to beperfect for prevention of delayed fracture.

DISCLOSURE OF THE INVENTION

An object of the present invention is to provide a method for preventingdelayed fracture of martensitic stainless steel which undergoesmartensitic transformation even when it is allowed to cool in air,without limiting the length of time from the completion of hot workingup to heat treatment for hardening.

Another object of the invention is to provide a method for preventingdelayed fracture which is applicable to martensitic stainless steelhaving an amount of effective dissolved C and N exceeding 0.45.

A still another object of the invention is to provide a method formanufacturing a martensitic stainless steel having improved resistanceto delayed fracture.

The present inventors made investigations with attention to the factthat a cause of delayed fracture in martensitic stainless steel residedin an increase in the material hardness and in the amount of occludedhydrogen both caused by dissolution of C and N in solid solution. As aresult, they found that the occurrence of delayed fracture can beprevented by carrying out preliminary softening heat treatment after hotworking. Subsequently, heat treatment for hardening can of course becarried out if necessary at any convenient time.

In one aspect, the present invention is a method for preventing delayedfracture of a martensitic stainless steel which undergoes a martensitictransformation when it is allowed to cool in air, characterized in thatafter hot working and prior to heat treatment by quenching from atemperature equal to or above the Ac₁ point of the steel, the steel issubjected to preliminary softening heat treatment under such conditionsthat the softening parameter P defined below is at least 15,400 and thesoftening temperature T is lower than the Ac₁ point:

P(softening parameter):P=T(20+log t)

-   -   T: softening temperature [K]    -   t: duration of softening treatment [Hr].

In another aspect, the present invention is a method for manufacturing ato martensitic stainless steel having improved resistance to delayedfracture, characterized in that a martensitic stainless steel consistingessentially of, in mass percent, C, 0.15-0.22%, Si: 0.05-1.0%, Mn:0.10-1.0%, Cr: 10.5-14.0%, P: at most 0.020%, S: at most 0.010%, Al: atmost 0.10%, Mo: 0-2.0%, V: at most 0.50%, Nb: 0-0.020%, Ca: 0-0.0050%,N: at most 0.1000%, and a remainder of Fe and impurities is subjected,after hot working, to preliminary softening heat treatment under suchconditions that the softening parameter P defined above is at least15,400 and the softening temperature T is lower than the Ac₁ point.

According to the present invention, in the manufacture of martensiticstainless steel pipes which are used in oil wells or the like, delayedfracture can be effectively prevented by subjecting them to preliminarysoftening heat treatment shortly after pipe formation, thereby making itpossible to subsequently perform heat treatment for hardening byquenching at an arbitrary time to form final products. As a result,there is no need to perform quenching within a limited period of timeafter pipe formation, and it is possible to prevent delayed fracture ofmartensitic stainless steel without obstruction of manufacturingoperations imposed by such limitation.

BRIEF EXPLANATION OF THE DRAWING

FIG. 1 is a graph showing the results of examples.

BEST MODE FOR CARRYING OUT THE INVENTION

The present invention will be explained below in connection with someparticular embodiments. However, the embodiments described below aremerely intended to illustrate the present invention and not intended torestrict it.

A steel which is of interest in the present invention includes, ingeneral, any martensitic stainless steel which undergoes martensitictransformation when it is allowed to cool in air.

However, in view of the main use of the steel as a steel pipe for use inan oil well, the following steel composition is preferred. In thisspecification, percent with respect to steel composition means masspercent unless otherwise indicated.

C, 0.15-0.22%

C (carbon) is one of the most important elements in martensiticstainless steel and is necessary to achieve a sufficient strength. The Ccontent is in the range of 0.15-0.22% in order to obtain well balancedstrength, yield ratio, and hardness. If the C content is less than0.15%, a sufficient strength cannot be obtained. If it exceeds 0.22%,the strength becomes too high, it becomes difficult to achieve asuitable balance of the strength with the yield ratio and the hardness.In addition, it results in a significant increase in the amount ofeffective dissolved C which is defined below, and there are cases thatdelayed fracture cannot be prevented even if preliminary softening heattreatment is performed thereon according to the present invention. Apreferred lower limit of the C content is 0.16% and a more preferredlower limit thereof is 0.18%.

Si: 0.05-1.0%

Si (silicon) is added as a deoxidizing agent for steel. In order toobtain this effect, at least 0.05% Si is added. In order to prevent adeterioration in toughness, its upper limit is 1.0%. Preferably thelower limit of Si content is 0.16% and more preferably it is 0.20%. Apreferred upper limit of Si content is 0.35%.

Mn: 0.10-1.0%

Like Si, Mn (manganese) has a deoxidizing action. However, addition oftoo much Mn causes toughness to deteriorate. For this reason, the Mncontent is 0.10-1.0%. Preferably it is at least 0.30%, and in order tomaintain toughness after quenching, it is preferably at most 0.60%.

Cr: 10.5-14.0%

Cr (chromium) is a fundamental element for obtaining the necessarycorrosion resistance in a martensitic stainless steel. By adding atleast 10.5% Cr, corrosion resistance with respect to pitting andcorrosion in time are improved, and corrosion resistance in aCO₂-containing environment is markedly increased. On the other hand, dueto the fact that Cr is a ferrite-forming element, if its content exceeds14.0%, δ ferrite forms easily during working at a high temperature,thereby causing hot workability to deteriorate and the strength afterhot working to decrease. The Cr content is preferably at least 12.0% andat most 13.1%.

P: at most 0.020%

Since the presence of too much P (phosphorus) as an impurity causestoughness to deteriorate, the P content is at most 0.020%.

S: at most 0.010%

The presence of too much S (sulfur) as an impurity causes not onlytoughness to deteriorate but also segregation to develop resulting inworsening of the quality of the inner surface of a steel pipe.Therefore, the S content is at most 0.010%.

Al: at most 0.10%

Al is present in steel as an impurity. If its content exceeds 0.10%,toughness worsens, so the Al content is at most 0.10%. Preferably it isat most 0.05%.

Mo: 0-2.0%

Mo (molybdenum) is an optional alloying element, but if Mo is added, ithas the effect of increasing strength and corrosion resistance. However,if the amount of Mo exceeds 2.0%, it becomes difficult for martensitictransformation to take place. Therefore, when added, the Mo content isat most 2.0%. Mo is an expensive alloying element, and addition of Mo inan increased amount is not efficient from an economic standpoint.Therefore, when it is added, its content is preferably made as small aspossible.

V: at most 0.50%

Addition of V (vanadium) has the effect of increasing the YR (yieldratio=yield strength/tensile strength) of steel. However, if the Vcontent exceeds 0.50%, it decreases toughness, so its upper limit is0.50%. V is an expensive alloying element and addition of V in anincreased amount is not efficient from an economic standpoint, so itsupper limit is preferably 0.30%.

Nb: 0-0.020%

Nb (niobium) is an optional alloying element. If Nb is added, it has theeffect of increasing strength. However, if the amount of Nb exceeds0.020%, it decreases toughness, so the upper limit of Nb is 0.020%. Nbis also an expensive alloying element, and addition of Nb in anincreased amount is not efficient from an economic standpoint.Therefore, when it is added, its content is preferably made as small aspossible.

Ca: 0-0.0050% Ca (calcium) is also an optional alloying element. Cacombines with S in the steel and has the effect of preventing hotworkability from decreasing due to segregation of S in grain boundaries.If Ca exceeds 0.0050%, inclusions in the steel increase and toughnessdecreases. Therefore, when it is added, its upper limit is 0.0050%.

N: at most 0.1000%

N (nitrogen) is an austenite stabilizing element, and like C, it is animportant element in a martensitic stainless steel, particularly inorder to improve the hot workability. If the amount of N exceeds0.1000%, toughness decreases. In addition, it results in a significantincrease in the amount of effective dissolved N, and as a result itbecomes very easy for delayed fracture to occur. Therefore, the upperlimit of N is 0.100%, and it is preferably 0.0500%. On the other hand,if the amount of N is too small, the efficiency of a denitrificationstep in steel making process worsens, thereby impeding the productivityof the steel. Therefore, the amount of N is preferably at least 0.0100%.

A remainder of the steel composition other than the above elementscomprises Fe and impurities such as Ti (titanium), B (boron), and(oxygen).

As described in the aforementioned JP 2004-43935A, susceptibility todelayed fracture of a martensitic stainless steel is influenced by theamount of effective dissolved C and N in the steel. Delayed fracturetends to easily occur if the sum of the effective dissolved C and 10times the effective dissolved N(C*+10N*) of the steel exceeds 0.45.Accordingly, the present invention exhibits its effects on a steel pipefor which the value of (C*+10N*) is greater than 0.45. In other words,in a steel with (C*+10N*)≦0.45, delayed fracture does not occur easily.

Accordingly, a method according to the present invention is particularlyeffective when it is applied to a steel with (C*+10N*)>0.45. Namely, incontrast to the invention described in JP 2004-43935A, the presentinvention need not control the amount of N in a steel so as to meet therequirement (C*+10N*)≦0.45. Thus, it is possible to sufficiently exploitthe effect of N at improving hot workability, thereby facilitating hotworking of martensitic stainless steel and favorably affecting theresulting hot worked products.

The amount of effective dissolved C and N (Q) is calculated as follows:

Q: Amount of effective dissolved C and N

Q=C*+10N*

C*: Amount of effective dissolved C

C*=C−[12{(Cr/52)×(6/23)}/10

N*: Amount of effective dissolved N

N*=N−[14{(V/51)+(Nb/93)}/10]−[14{(Ti/48)+(B/11)+(Al/27)}/10]

In the above formulas, each element indicates its content in masspercent.

According to the present invention, a martensitic stainless steel havinga composition as described above is subjected, after hot working such aspipe formation, to preliminary softening heat treatment in order toprevent delayed fracture from occurring subsequently. The cause ofdelayed fracture of a martensitic stainless steel is nitrogen andhydrogen which are captured in strains which are introduced during hotworking. Therefore, if these occluded gases are released, delayedfracture can be prevented. For this purpose, preliminary softeningtreatment is carried out under such conditions that the softeningparameter P which is calculated by the following formula is at least15,400 and the softening temperature T is lower than the Ac₁ point.

P(softening parameter):P=T(20+log t)

-   -   T: softening temperature [K]    -   t: duration of softening treatment [Hr].

In order to prevent delayed fracture, it is necessary to decrease theamount of occluded hydrogen and nitrogen in steel. For this purpose, thehardness of the steel is decreased by softening heat treatment. If thesoftening parameter is less than 15,400 after the softening heattreatment, softening is inadequate, and even after carrying outsoftening heat treatment, there is the possibility of delayed fractureoccurring. However, even in the case where the steel is heat treated soas to have a softening parameter of 15,400 or larger, if the softeningtemperature which is the temperature at which the softening heattreatment is carried out is equal to or greater than the Ac₁ point ofthe steel, the structure again becomes an austenite phase, and aftercooling, a martensitic structure which has not undergone softening heattreatment appears so that delayed fracture tends to occur.

The preliminary softening heat treatment is carried out after hotworking and before final heat treatment for hardening by quenching froma temperature of at least the Ac₁ point of the steel. It can beconducted any time within this period as long as delayed fracture hasnot occurred. However, since the possibility of delayed fractureoccurring is increased after the time elapsed from the completion of thefinal hot working (e.g., pipe making) (excluding the subsequent coolingtime) is 168 hours, it is preferable to perform preliminary softeningheat treatment within 168 hours from the final hot working. Preliminarysoftening heat treatment may be carried out immediately after the finalhot working. For example, it can be conducted immediately after the hotworked product is allowed to cool in air or even while it is beingallowed to cool and after the temperature of the steel is decreased tothe M_(f) point of the steel at which martensitic transformation hasbeen completed or lower.

The preliminary softening heat treatment is performed by heating the hotworked product to a softening temperature T which is lower than the Ac₁point of the steel and maintaining the temperature for a certain period.The duration of this heat treatment is the duration of softeningtreatment “t” in the above formula, so it is selected depending on thesoftening temperature T such that the softening parameter P calculatedby the above formula is at least 15,400. Cooling after softening heattreatment is preferably performed by allowing to cool in air.

After the preliminary softening heat treatment is performed on a hotworked martensitic stainless steel, the steel is reliably prevented fromundergoing delayed fracture, so the final heat treatment for hardeningby quenching can be performed at any convenient point of time. As aresult, a plurality of hot worked steel products capable of beinghardened by quenching from the same temperature can be consecutivelysubjected to the final heat treatment for hardening, thereby making itpossible to reduce the temperature variations of a heat treatmentfurnace, and hence improve the manufacturing efficiency and save theoperational costs.

As described above, the ease of occurrence of delayed fracture isinfluenced by the amount of effective dissolved C and N. According tothe present invention, regardless of this amount (namely, even if theamount of effective dissolved C and N is considerably large), delayedfracture can be prevented.

Hot working and final heat treatment for hardening (quenching) of amartensitic stainless steel can be performed in a conventional manner.For example, hot working may be carried out by pipe formation underconditions which are generally employed in the manufacture of seamlesspipes. Final heat treatment is generally performed by quenching from atemperature in the range of 920-980° C. and subsequent tempering in thetemperature range of 650-750° C.

Example

Mannesmann pipe manufacture was carried out on billets of martensiticstainless steels having the compositions (balance: Fe and impurities)shown in Table 1 to form seamless steel pipes with 60.33 mm in outerdiameter and 4.83 mm in wall thickness.

A test piece having a length of 250 mm was taken from each of theresulting seamless pipes for use in a drop weight test. A weight of 150kg with a tip having a curvature of 90 mm was dropped onto each testpiece from a height of 0.2 m to impart deformation from an impact load(294 J). Thereafter, the test piece was subjected to preliminarysoftening heat treatment under the two conditions (1) and (2) shown inTable 2 with respect to the temperature of the heat treating furnace(softening temperature) and the residence therein (duration of softeningtreatment). The value of softening parameter calculated from eachcondition is also shown in Table 2. The reason why the impact load wasapplied prior to preliminary softening heat treatment is for the purposeof simulating handling damage during transport of a steel pipe in anactual manufacturing process.

Each test piece which had been heat treated for softening was left inair for 720 hours, and the presence or absence of cracks wasinvestigated. Cracks were ascertained by visual observation andultrasonic testing. The results are shown in Table 2 and FIG. 1.

The amount of effective dissolved C and N (Q) in each steel wascalculated by the following formulas and is shown in Table 1 along withits Ac₁ point:

Q=(C*+10N*)

C*=C−[12{(Cr/52)×(6/23)}/10, and

N*=N−[14{(V/51)+(Nb/93)}/10]−[14{(Ti/48)+(B/11)+(Al/27)}/10].

From FIG. 1, it can be seen that delayed fracture does not occur whenQ≦0.45, and when Q>0.45, delayed fracture can be prevented by making thesoftening parameter at least 15,400. Thus, in contrast with the teachingin JP 2004-43935 in which the condition of Q≦0.45 must be satisfied inorder to prevent delayed fracture, the present invention makes itpossible to prevent delayed fracture even with steels having a Q valuelarger than 0.45.

TABLE 1 Ac1 point No. C Si Mn P S Cr Mo V Ti Nb Al Ca B N C* + 10N* (°C.) 1 0.19 0.42 0.92 0.019 0.0043 12.54 0.01 0.05 0.001 0.001 0.0020.0003 0.0004 0.0371 0.461 807 2 0.16 0.37 0.47 0.019 0.0008 12.88 0.010.04 0.004 0.003 0.001 0.0023 0.0001 0.0393 0.455 799 3 0.16 0.27 0.360.013 0.0012 12.60 0.03 0.03 0.004 0.002 0.011 0.0007 0.0005 0.04720.510 801 4 0.19 0.24 0.90 0.013 0.0005 12.80 0.01 0.04 0.002 0.0010.002 0.0053 0.0003 0.0387 0.479 807 5 0.19 0.23 0.88 0.014 0.0024 12.560.02 0.05 0.003 0.002 0.004 0.0008 0.0006 0.0451 0.533 807 6 0.19 0.220.73 0.012 0.0042 12.68 0.02 0.08 0.003 0.002 0.015 0.0012 0.0002 0.04710.518 809 7 0.20 0.21 0.78 0.012 0.0006 12.70 0 0.13 0.002 0.001 0.0010.0007 0.0003 0.0453 0.533 808 8 0.18 0.34 0.08 0.010 0.0034 12.51 0.010.06 0.006 0.001 0.009 0.0020 0.0003 0.0391 0.445 806 9 0.17 0.31 0.400.018 0.0026 12.58 0.01 0.07 0.002 0.002 0.036 0.0014 0.0003 0.03040.281 805 10 0.19 0.28 0.51 0.016 0.0009 12.89 0.02 0.03 0.001 0.0010.012 0.0003 0.0006 0.0219 0.286 808 11 0.20 0.30 0.88 0.020 0.001212.53 0.01 0.07 0.001 0.001 0.036 0.0003 0.0001 0.0394 0.404 809 12 0.180.23 0.67 0.013 0.0005 12.55 0 0.04 0.003 0.002 0.002 0 0.0002 0.01570.239 803 13 0.17 0.26 0.89 0.014 0.0010 12.50 0 0.17 0.001 0 0.0160.0026 0.0007 0.0443 0.444 798 14 0.20 0.22 0.92 0.015 0.0009 12.50 0.020.13 0.002 0 0.010 0.0005 0.0012 0.0364 0.417 807 15 0.19 0.27 0.590.016 0.0031 12.61 0 0.05 0.012 0.001 0.046 0.0013 0.0009 0.0236 0.194805 16 0.20 0.22 0.52 0.014 0.0005 13.00 0 0.05 0.003 0.001 0.003 0.00040.0002 0.0313 0.407 808

TABLE 2 Conditions for softening heat treatment (1) Conditions forsoftening heat treatment (2) Temperature Duration Softening TestTemperature Duration Softening Test No. C* + 10N* (° C.) (min) parameterresults (° C.) (min) parameter results  1 0.461 550 10 15820 ◯ This 73025 19679 ◯ This  2 0.455 630 20 17629 ◯ invention 705  5 18505 ◯invention  3 0.510 560 20 16263 ◯ 820 15 21202 X Compar.  4 0.479 480 1014474 X Compar- 590 10 16588 ◯ This  5 0.533 500 25 15166 X ative 680 1518486 ◯ invention  6 0.518 400 20 13139 X 810 15 21008 X Compar.  70.533 450 30 14242 X 530 10 15435 ◯ Inventive  8 0.445 360 15 12279 ◯500 20 15091 ◯ Compar-  9 0.281 520 25 15558 ◯ 750 15 19844 ◯ ative 100.286 350 15 12085 ◯ 430 20 13725 ◯ 11 0.404 380 10 12552 ◯ 790 45 21127◯ 12 0.239 380 15 12667 ◯ 560 15 16158 ◯ 13 0.444 550 30 16212 ◯ 800  520302 ◯ 14 0.417 460 10 14090 ◯ 500 60 15460 ◯ 15 0.194 390 30 13060 ◯780 60 21060 ◯ 16 0.407 590 10 16588 ◯ 700 25 19090 ◯

1-5. (canceled)
 6. A method for manufacturing a martensitic stainlesssteel comprising the steps of: hot working a steel composition; coolingthe hot-worked steel to a temperature lower than the Ms point to form amartensitic steel; carrying out preliminary softening heat treatment tothe resulting martensitic steel by heating it to a temperature lowerthan Ac₁ point; heating the resulting steel to a temperature equal to orabove the Ac₁ point of the steel; quenching by cooling the steel fromthe temperature equal to or above the Ac₁ point of the steel; and,tempering the resulting quenched steel, said preliminary softening heattreatment is carried out under such conditions that the softeningparameter P defined below is at least 15,400 and the softeningtemperature T is lower than the Ac₁ point:P(softening parameter):P=T(20+log t) T: softening temperature [K] t:duration of softening treatment [Hr].
 7. A method for manufacturing amartensitic stainless steel set forth in claim 6 wherein the martensiticstainless steel has a steel composition consisting essentially of, inmass percent, C, 0.15-0.22%, Si: 0.05-1.0%, Mn: 0.10-1.0%, Cr:10.5-14.0%, P: at most 0.020%, S: at most 0.010%, Al: at most 0.10%, Mo:0-2.0%, V: at most 0.50%, Nb: 0-0.020%, Ca: 0-0.0050%, N: at most0.1000%, and a remainder of Fe and impurities.
 8. A method formanufacturing a martensitic stainless steel as recited in claim 7wherein the steel composition is such that the amount of effectivedissolved C and N (=[C*+10N*]) where C* and N* are calculated by thefollowing formulas is larger than 0.45:C*=C−[12{(Cr/52)×(6/23)}/10], andN*=N−[14{(V/51)+(Nb/93)}/10]−[14{(Ti/48)+(B/11)+(Al/27)}/10].
 9. Amethod for manufacturing a martensitic stainless steel as set forth inany of claim 6 wherein the preliminary softening heat treatment isperformed within 168 hours after final hot working.
 10. A method formanufacturing a martensitic stainless steel as set forth in claim 9wherein the hot working is pipe formation.
 11. A method of manufacturinga martensite steel as set forth in claim 6 wherein the quenching iscarried out by heating to a temperature of 920-980° C. and cooling themartensite steel.
 12. A method of manufacturing a martensite steel a setforth in claim 6 wherein the tempering is carried out by heating themartensite steel to a temperature of 650-750° C.
 13. A method formanufacturing a martensitic stainless steel as set forth in any of claim7 wherein the preliminary softening heat treatment is performed within168 hours after final hot working.
 14. A method for manufacturing amartensitic stainless steel as set forth in any of claim 8 wherein thepreliminary softening heat treatment is performed within 168 hours afterfinal hot working.
 15. A method of manufacturing a martensite steel asset forth in claim 7 wherein the quenching is carried out by heating toa temperature of 920-980° C. and cooling the martensite steel.
 16. Amethod of manufacturing a martensite steel as set forth in claim 8wherein the quenching is carried out by heating to a temperature of920-980° C. and cooling the martensite steel.